pith. sign in

arxiv: 1907.11390 · v1 · pith:6WOUGGAFnew · submitted 2019-07-26 · ❄️ cond-mat.mtrl-sci

Plate-like precipitate effects on plasticity of Al-Cu micro-pillar: {100}-interfacial slip

Peng Zhang , Jian-Jun Bian , Chong Yang , Jin-Yu Zhang , Gang Liu , J\'er\^ome Weiss , Jun Sun This is my paper

Pith reviewed 2026-05-24 15:49 UTC · model grok-4.3

classification ❄️ cond-mat.mtrl-sci
keywords Al-Cu alloysθ' precipitatesinterfacial slip{100} slipdislocation cross-slipkink-pair mechanismmicro-pillarsplasticity
0
0 comments X

The pith

Screw dislocations cross-slip from {111} to {100} precipitate interfaces in Al-Cu, enabling room-temperature {100} slip along coherent boundaries.

A machine-rendered reading of the paper's core claim, the machinery that carries it, and where it could break.

The paper examines plasticity in Al-Cu micro-pillars sized so that plate-like θ'-Al2Cu precipitates span the entire sample. It reports the first observation of {100}-slip traces in aluminum and its alloys at room temperature. These traces are shown to lie along the coherent θ'-Al2Cu/α-Al matrix interface rather than conventional {111} planes. Molecular dynamics simulations combined with stress analysis demonstrate that screw dislocations cross-slip onto the interface and advance by a kink-pair mechanism. The work further shows within the Peierls-Nabarro model that the interface stabilizes the {100} screw dislocations against core spreading while raising the Peierls stress.

Core claim

In Al-Cu micro-pillars containing spanning θ'-Al2Cu precipitates, {100}-slip traces appear at room temperature for the first time in Al or Al alloys. These slips operate along the coherent precipitate/matrix interface. Screw dislocations cross-slip from {111} planes onto the {100} interface and move by kink-pair nucleation and propagation, as indicated by molecular dynamics and stress analysis. The interface stabilizes the {100} screw dislocations from core spreading and elevates the Peierls stress according to the Peierls-Nabarro framework. This accounts for the observed plasticity and points to a larger role for interfacial slip in Al-Cu alloys at elevated temperature via the kink-pair law

What carries the argument

Cross-slip of screw dislocations from {111} planes onto the coherent {100} θ'-Al2Cu/α-Al interface followed by kink-pair motion on that interface.

If this is right

  • {100} interfacial slip contributes measurably to room-temperature plasticity when precipitates span the sample.
  • The kink-pair mechanism on the interface implies stronger temperature dependence of this slip mode than conventional glide.
  • The interface raises the Peierls stress for {100} screws, altering the stress required to sustain the new slip system.
  • Interfacial slip is expected to become more prominent in Al-Cu alloys at elevated temperature.

Where Pith is reading between the lines

These are editorial extensions of the paper, not claims the author makes directly.

  • If kink-pair motion controls the rate, then {100} slip should accelerate faster with temperature than slip on {111} planes.
  • The stabilization of {100} cores at coherent interfaces may occur in other FCC systems containing plate-like precipitates.
  • Alloy design could deliberately tune precipitate coherence or spacing to promote or suppress this slip path.

Load-bearing premise

The observed slip traces must be accurately indexed as strictly {100} and confined to the coherent precipitate-matrix interface; misindexing or loss of coherence would remove the basis for the interfacial mechanism.

What would settle it

High-resolution slip-trace or TEM analysis of the same micro-pillars showing the traces deviate from the {100} interface planes or lie on {111} planes instead.

Figures

Figures reproduced from arXiv: 1907.11390 by Chong Yang, Gang Liu, J\'er\^ome Weiss, Jian-Jun Bian, Jin-Yu Zhang, Jun Sun, Peng Zhang.

Figure 1
Figure 1. Figure 1: Precipitates in the aged Al-Cu alloy. (a) TEM image of the aged Al-Cu alloy, taken along the {100}- direction. The inset gives the distribution of measured precipitate diameters. (b) HRTEM image of ￾′-Al2Cu pre￾cipitate, showing a thickness of ~ 15 nm. The corrected average diameter ￾￾ is ~ 978 nm, very close to the diameter of micro-pillars (1000 nm, see Fig. 2a). Consequently, the plate-like precipitates… view at source ↗
read the original abstract

In this paper, we study the effects of $\theta ^\prime$-Al$_2$Cu plate-like precipitates on the plasticity of Al-Cu micro-pillars, with a sample size allowing the precipitates to cross the entire micro-pillar. {100}-slip traces are identified for the first time in Al and Al alloys at room temperature. We investigate the underlying mechanisms of this unusual {100}-slip, and show that it operates along the coherent $\theta ^\prime$-Al$_2$Cu precipitate/$\alpha$-Al matrix interface. A combination of molecular dynamics simulations and stress analysis indicates that screw dislocations can cross-slip from the {111} plane onto the {100} $\theta ^\prime$-Al$_2$Cu/$\alpha$-Al interface, then move on it through a kink-pair mechanism, providing a reasonable explanation to the observed {100}-slips. The roles of the $\theta ^\prime$-Al$_2$Cu/$\alpha$-Al matrix interface on the properties of interfacial dislocations are studied within the Peierls-Nabarro framework, showing that the interface can stabilize the {100} screw dislocations from the spreading of the core, and increases the Peierls stress. These results improve our understanding of the mechanical behavior of Al-Cu micro-pillars at room temperature, and imply an enhanced role of interfacial slip in Al-Cu based alloys at elevated temperature in consideration of the underlying kink-pair mechanism.

Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, simulated authors' rebuttal, and a circularity audit. Tearing a paper down is the easy half of reading it; the pith above is the substance, this is the friction.

Referee Report

2 major / 2 minor

Summary. The paper studies the effects of θ'-Al₂Cu plate-like precipitates on plasticity in Al-Cu micro-pillars sized so that precipitates span the pillar cross-section. It reports the first observation of {100}-slip traces in Al and Al alloys at room temperature and attributes them to interfacial slip on the coherent θ'-Al₂Cu/α-Al {100} interface. The proposed mechanism is that screw dislocations cross-slip from {111} planes onto the interface and propagate by a kink-pair process, supported by molecular dynamics simulations and Peierls-Nabarro analysis showing that the interface stabilizes the {100} screw core and raises the Peierls stress.

Significance. If the experimental indexing of the slip traces holds, the result would be significant for identifying a previously unreported slip mode in aluminum alloys at ambient temperature and for highlighting the role of coherent interfaces in enabling non-conventional dislocation motion, with implications for precipitate strengthening and high-temperature deformation where the kink-pair mechanism may become rate-controlling.

major comments (2)
  1. [Abstract, paragraph on slip trace analysis] Abstract, paragraph on slip trace analysis: the central claim requires that the observed surface traces are produced by slip strictly on {100} planes lying at the coherent θ'-Al₂Cu/α-Al interface. The manuscript must supply quantitative details on (i) how the pillar crystallographic orientation was determined, (ii) the measured trace angles relative to the free surface with associated uncertainties, and (iii) confirmation that traces terminate at or follow the precipitate habit plane; without these, modest angular error could allow re-indexing to conventional {111} slip that intersects the interface.
  2. [MD simulations and Peierls-Nabarro analysis sections] MD simulations and Peierls-Nabarro analysis sections: the interatomic potential is listed among the free parameters, yet no validation against experimental lattice parameters, stacking-fault energies, or known Peierls stresses for Al or Al-Cu is reported, nor are error bars on the simulated cross-slip barriers or kink-pair energies provided. These omissions are load-bearing because the proposed mechanism rests on the quantitative outcome of the simulations.
minor comments (2)
  1. The abstract mixes experimental observations and simulation interpretations without clear separation; a short sentence distinguishing the two would improve readability.
  2. Figure captions should explicitly state the viewing direction and surface normal for each micro-pillar image to aid trace indexing.

Simulated Author's Rebuttal

2 responses · 0 unresolved

We thank the referee for the careful and constructive review. We address each major comment below and will revise the manuscript to incorporate the requested details and validations.

read point-by-point responses

  1. Referee: [Abstract, paragraph on slip trace analysis] Abstract, paragraph on slip trace analysis: the central claim requires that the observed surface traces are produced by slip strictly on {100} planes lying at the coherent θ'-Al₂Cu/α-Al {100} interface. The manuscript must supply quantitative details on (i) how the pillar crystallographic orientation was determined, (ii) the measured trace angles relative to the free surface with associated uncertainties, and (iii) confirmation that traces terminate at or follow the precipitate habit plane; without these, modest angular error could allow re-indexing to conventional {111} slip that intersects the interface.

    Authors: We agree that quantitative details are essential to rigorously support the {100} indexing and rule out alternative interpretations. In the revised manuscript we will add: (i) a description of the orientation determination method (EBSD on the pillar top surface), (ii) tabulated trace angles measured from multiple SEM images with associated uncertainties (standard deviations from repeated measurements), and (iii) magnified images and line-profile analysis confirming that the traces align with and terminate precisely at the θ' habit planes. These additions will be placed in a dedicated subsection of the experimental methods and results. revision: yes

  2. Referee: [MD simulations and Peierls-Nabarro analysis sections] MD simulations and Peierls-Nabarro analysis sections: the interatomic potential is listed among the free parameters, yet no validation against experimental lattice parameters, stacking-fault energies, or known Peierls stresses for Al or Al-Cu is reported, nor are error bars on the simulated cross-slip barriers or kink-pair energies provided. These omissions are load-bearing because the proposed mechanism rests on the quantitative outcome of the simulations.

    Authors: We concur that explicit validation and uncertainty quantification strengthen the simulation claims. We will insert a new paragraph in the methods section that validates the chosen interatomic potential against experimental lattice parameters, stacking-fault energies, and literature Peierls stresses for pure Al and Al-Cu. We will also report statistical uncertainties (standard errors from at least five independent runs) on the computed cross-slip barriers and kink-pair formation energies, together with a brief sensitivity check using an alternative potential where feasible. revision: yes

Circularity Check

0 steps flagged

No circularity; central claim rests on independent experimental indexing plus standard MD/Peierls-Nabarro analysis

full rationale

The derivation proceeds from direct observation of slip traces in micro-pillars, followed by application of off-the-shelf molecular dynamics and the Peierls-Nabarro framework to interpret cross-slip and kink-pair motion. Neither the experimental indexing nor the simulation outputs are defined in terms of the final mechanism; the frameworks are externally established and do not reduce the claimed interfacial {100} slip to a fitted parameter or self-citation that presupposes the result. No load-bearing step matches any of the enumerated circularity patterns.

Axiom & Free-Parameter Ledger

1 free parameters · 1 axioms · 0 invented entities

The claim rests on standard interatomic potentials in MD (empirically fitted) and the assumption of a perfectly coherent interface whose properties are taken from prior literature; no new entities are postulated.

free parameters (1)
  • interatomic potential parameters
    MD simulations of dislocation motion require empirical potentials whose parameters are fitted to bulk properties or DFT data.
axioms (1)
  • domain assumption The θ'-Al2Cu/α-Al interface remains coherent under the applied stresses in micro-pillars
    Invoked to allow interfacial slip and stabilization of {100} screw dislocations in both MD and Peierls-Nabarro sections.

pith-pipeline@v0.9.0 · 5818 in / 1276 out tokens · 25684 ms · 2026-05-24T15:49:04.252934+00:00 · methodology

discussion (0)

Sign in with ORCID, Apple, or X to comment. Anyone can read and Pith papers without signing in.

Reference graph

Works this paper leans on

54 extracted references · 54 canonical work pages · 1 internal anchor

  1. [1]

    W. Sun, Y . Zhu, R. Marceau, L. Wang, Q. Zhang, X. Gao, C. Hutchinson, Precipitation strengthening of aluminum alloys by room - temperature cyclic plasticity, Science 363(6430) (2019) 972 - 975

    work page 2019

  2. [2]

    Y . Lin, Z. Zheng, S. Li, X. Kong, Y . Han, Microstructures and properties of 2099 Al - Li alloy, Materials Characterization 84 (2013) 88 - 99

    work page 2099

  3. [3]

    Nie, B.C

    J.F. Nie, B.C. Muddle, Strengthening of an Al - Cu - Sn alloy by deformation - resistant precipitate plates, Acta Materialia 56(14) (2008) 3490 - 3501

    work page 2008

  4. [4]

    Bourgeois, C

    L. Bourgeois, C. Dwyer, M. Weyland, J. - F. Nie, B.C. Muddle, Structure and energetics of the coherent interface between the θ ′ preci pitate phase and aluminium in Al – Cu, Acta Materialia 59(18) (2011) 7043 - 7050

    work page 2011

  5. [5]

    Z. Liu, S. Bai, X. Zhou, Y . Gu, On strain - induced dissolution of θ ′ and θ particles in Al – Cu binary alloy during equal channel angular pressing, Materials Science and Enginee ring: A 528(6) (2011) 2217 - 2222. 22

    work page 2011

  6. [6]

    B.A. Chen, G. Liu, R.H. Wang, J.Y . Zhang, L. Jiang, J.J. Song, J. Sun, Effect of interfacial solute segregation on ductile fracture of Al - Cu - Sc alloys, Acta Materialia 61(5) (2013) 1676 - 1690

    work page 2013

  7. [7]

    Russell, M.F

    K.G. Russell, M.F. Ashb y, Slip in aluminum crystals containing strong, plate - like particles, Acta Metallurgica 18(8) (1970) 891 - 901

    work page 1970

  8. [8]

    Calabrese, C

    C. Calabrese, C. Laird, Cyclic stress — strain response of two - phase alloys Part II. Particles not penetrated by dislocations, Materials Science & Engineering 13(2) (1974) 159 - 174

    work page 1974

  9. [9]

    H. Liu, Y . Gao, L. Qi, Y . Wang, J. - F. Nie, Phase - Field Simulation of Orowan Strengthening by Coherent Precipitate Plates in an Aluminum Alloy, Metallurgical and Materials Transactions A 46(7) (2015) 3287 - 3301. [10] M. Murayama, Z. Horita, K. Hono, Microstructure of two - phase Al - 1.7 at% Cu alloy deformed by equal - channel angular pressing, Act...

    work page 2015

  10. [10]

    Plate-like precipitate effects on plasticity of Al-Cu alloys at micrometer to submicrometer scales

    P. Zhang, J. J . Bian, J.Y . Zhang, G. Liu, J. Weiss, J. Sun, Plate - like precipitate effects on plasticity of Al - Cu alloys at micrometer to sub - micrometer scales, arXiv:1907.09818 (2019)

    work page internal anchor Pith review Pith/arXiv arXiv 1907

  11. [11]

    Kaira, C

    C.S. Kaira, C. Kantzos, J.J. Williams, V . De Andrade, F. De Carlo, N. Chawla, Microstructural evolution and deformation behavior of Al - Cu alloys: A transmission X - ray microscopy (TXM) and micropillar compression study, Acta Materialia (2017)

    work page 2017

  12. [12]

    S. - H. Li, W. - Z. Han, J. Li, E. Ma, Z. - W. Shan, Small - volume aluminum alloys with native oxide shell deliver unprecedented strength and toughne ss, Acta Materialia 126 (2017) 202 - 209

    work page 2017

  13. [13]

    R. Gu, A. Ngan, Size effect on the deformation behavior of duralumin micropillars, Scripta Materialia 68(11) (2013) 861 - 864

    work page 2013

  14. [14]

    Servi, J.T

    I.S. Servi, J.T. Norton, N.J. Grant, Some observations of subgrain formation duri ng creep in high purity aluminum, JOM , 4(9) (1952) 965 - 971

    work page 1952

  15. [15]

    C. J. Beevers, R. W.K . Honeycombe, Cubic slip in aluminium alloy crystals, Acta Metallurgica , 9(5) (1961) 513 - 515

    work page 1961

  16. [16]

    Le Hazif, P

    R. Le Hazif, P. Dorizzi Et, J.P. Poirier, Glissement {110} 〈 110 〉 dans les metaux de structure cubique a faces centrees, Acta Metallurgica 21(7) (1973) 903 - 911

    work page 1973

  17. [17]

    Carrard, J.L

    M. Carrard, J.L. Martin, A study of (001) glide in [112] aluminium single crystals, Philosophical Magazine A 56(3) (1987) 391 - 405

    work page 1987

  18. [18]

    Carrard, J.L

    M. Carrard, J.L. Martin, II. Microscopic mechanism, Philosophical Magazine A 58(3) (1988) 491 - 505

    work page 1988

  19. [19]

    Caillard, J

    D. Caillard, J. L. Martin, Glide of dislocations in non - octahedral planes of fcc metals: a review, International Journal of Materials Research 100(10) (2009) 1403 - 1410

    work page 2009

  20. [20]

    H. P . Karnthaler, The study of glide on {001} planes in fcc metals deformed at room temperature, Philosophical Magazine A , 38(2) (1978) 141 - 156

    work page 1978

  21. [21]

    Arzaghi, B

    M. Arzaghi, B. Beausir, L.S. Tóth, Contribution of non - octahedral slip to t exture evolution of fcc polycrystals in simple shear, Acta Materialia 57(8) (2009) 2440 - 2453

    work page 2009

  22. [22]

    Maurice, J.H.J.A.M

    C. Maurice, J.H.J.A.M. Driver, Hot rolling textures of f.c.c. metals — Part I. Experimental results on Al single and polycrystals, 45(11) (1997) 4627 - 4638. [24 ] S. Plimpton, Fast parallel algorithms for short - range molecular dynamics, Journal of computational physics 117(1) (1995) 1 - 19

    work page 1997

  23. [23]

    Apostol, Y

    F. Apostol, Y . Mishin, Interatomic potential for the Al - Cu system, Physical Review B 83(5) (2011) 054116

    work page 2011

  24. [24]

    Berend sen, J.v

    H.J. Berend sen, J.v. Postma, W.F. van Gunsteren, A. DiNola, J. Haak, Molecular dynamics with coupling to an external bath, The Journal of chemical physics 81(8) (1984) 3684 - 3690

    work page 1984

  25. [25]

    Bulatov, W

    V . Bulatov, W. Cai, Computer simulations of dislocations, Oxford University Press o n Demand , 2006

    work page 2006

  26. [26]

    Hartford, B

    J. Hartford, B. V on Sydow, G. Wahnstrom, B.I. Lundqvist, Peierls barriers and stresses for edge dislocations in Pd and Al calculated from first principles, Physical Review B 58(5) (1998) 2487 - 2496

    work page 1998

  27. [27]

    Peierls, The size of a disloc ation, Proceedings of the Physical Society 52(1) (1940) 34 - 37

    R. Peierls, The size of a disloc ation, Proceedings of the Physical Society 52(1) (1940) 34 - 37

    work page 1940

  28. [28]

    Nabarro, Dislocations in a simple cubic lattice, Proceedings of the Physical Society 59(2) 23 (1947) 256

    F.R.N. Nabarro, Dislocations in a simple cubic lattice, Proceedings of the Physical Society 59(2) 23 (1947) 256

    work page 1947

  29. [29]

    B. Joós, Q. Ren, M.S. Duesbery, Peierls - Nabarro model of dislocations in silicon with generalized stacking - fault restoring forces, Physi cal Review B 50(9) (1994) 5890 - 5898

    work page 1994

  30. [30]

    Ludwig, E

    W. Ludwig, E. Pereiro - López, D. Bellet, In situ investigation of liquid Ga penetration in Al bicrystal grain boundaries: grain boundary wetting or liquid metal embrittlement?, Acta Materialia 53(1) (2005) 151 - 162

    work page 2005

  31. [31]

    H. - S. Nam, D.J. Srolovitz, Effect of material properties on liquid metal embrittlement in the Al – Ga system, Acta Materialia 57(5) (2009) 1546 - 1553

    work page 2009

  32. [32]

    S. Lee, J. Jeong, Y . Kim, S.M. Han, D. Kiener, S.H. Oh, FIB - induced dislocations in Al submicron p illars: Annihilation by thermal annealing and effects on deformation behavior, Acta Materialia 110 (2016) 283 - 294

    work page 2016

  33. [33]

    Unocic, M.J

    K.A. Unocic, M.J. Mills, G.S. Daehn, Effect of gallium focused ion beam milling on preparation of aluminium thin foils, Journal of M icro scopy 240(3) (2010) 227 - 38

    work page 2010

  34. [34]

    Zhang, J

    R.F. Zhang, J. Wang, I.J. Beyerlein, T.C. Germann, Dislocation nucleation mechanisms from fcc/bcc incoherent interfaces, Scripta Materialia 65(11) (2011) 1022 - 1025

    work page 2011

  35. [35]

    Wang, R.G

    J. Wang, R.G. Hoagland, J.P. Hirth, A. Misra, Atomist ic simulations of the shear strength and sliding mechanisms of copper – niobium interfaces, Acta Materialia 56(13) (2008) 3109 - 3119

    work page 2008

  36. [36]

    Uchic, D.M

    M.D. Uchic, D.M. Dimiduk, J.N. Florando, W.D. Nix, Sample dimensions influence strength and crystal plasticity, Science 305(5686) (2004) 986 - 989

    work page 2004

  37. [37]

    Greer, W.C

    J.R. Greer, W.C. Oliver, W.D. Nix, Size dependence of mechanical properties of gold at the micron scale in the absence of strain gradients, Acta Materialia 53(6) (2005) 1821 - 1830

    work page 2005

  38. [38]

    Hirth, J

    J.P. Hirth, J. Lothe, Theory of dislocat ions, J. Wiley , 1968

    work page 1968

  39. [39]

    D. M. Barnett, J. Lothe, An image force theorem for dislocations in anisotropic bicrystals, Journal of Physics F: metal physics , 4(10) (1974) 1618

    work page 1974

  40. [40]

    Kroupa, L

    F. Kroupa, L. Lejček, Splitting of dislocations in the Peierls - Nabarro model, Czechoslovak Journal of Physics B 22(9) (1972) 813 - 825

    work page 1972

  41. [41]

    B. Joos, Q. Ren, M.S. Duesbery, Peierls - Nabarro model of dislocations in silicon with generalized stacking - fault restoring forces, Physical Review B 50(9) (1994) 5890 - 5898

    work page 1994

  42. [42]

    Hartford, B

    J. Hartford, B. V on Sydow, G. Wahnström, B. I. Lundqvist, Peierls barriers and stresses for edge dislocations in Pd and Al calculated from first principles, Physical Review B 58(5) (1998) 2487

    work page 1998

  43. [43]

    Ferré, P

    D. Ferré, P. Carrez, P. Cordier, Modeling dislocatio n cores inSrTiO3using the Peierls - Nabarro model, Physical Review B 77(1) (2008)

    work page 2008

  44. [44]

    Schoeck, The core structure of dislocations

    G. Schoeck, The core structure of dislocations. Peierls model vs. atomic simulations in Pd, Computational M aterials S cience 21(1) (2001) 124 - 134

    work page 2001

  45. [45]

    Edagawa, Y

    K. Edagawa, Y . Kami mura, A.M. Iskandarov, Y . Umeno, S. Takeuchi, Peierls stresses estimated by a discretized Peierls – Nabarro model for a variety of crystals, Materialia 5 (2019)

    work page 2019

  46. [46]

    Rodney, L

    D. Rodney, L. Ventelon, E. Clouet, L. Pizzagalli, F. Willaime, Ab initio modeling of disloc ation core properties in metals and semiconductors, Acta Materialia 124 (2017) 633 - 659

    work page 2017

  47. [47]

    Mills, P

    M.J. Mills, P. Stadelmann, A study of the structure of Lomer and 60° dislocations in aluminium using high - resolution transmission electron microscopy, Philosophica l Magazine A 60(3) (1989) 355 - 384

    work page 1989

  48. [48]

    G. Lu, N. Kioussis, E. Kaxiras, V .V . Bulatov, Generalized Stacking Fault Energy Surface and Dislocation Properties of Aluminum: A First - Principles Theoretical Study, (1998)

    work page 1998

  49. [49]

    Joos, M.S

    B. Joos, M.S. Duesbery, T he Peierls stress of dislocations : an analytical formula , Physical Review Letters 78(2) (1997) 266 - 269

    work page 1997

  50. [50]

    Hoellerbauer, H

    W. Hoellerbauer, H. Karnthaler, In Situ Deformation of(001) Aluminum Foils, Seventh Eur. Congr. Electron Microsc. (1980) 260 - 261

    work page 1980

  51. [51]

    Misra, M

    A. Misra, M. Verdier, H. Kung, J.D. Embury, J.P. Hirth, Deformation mechanism maps for polycrystalline metallic multiplayers, Scripta Materialia 41(9) (1999) 973 - 979

    work page 1999

  52. [52]

    Zhang, G

    J. Zhang, G. Liu, J. Sun, Crystallization - aided extraordinary plastic deformation in nanolayered 24 crystalline Cu/amorphous Cu - Zr micropillars, Scientific reports 3 (2013)

    work page 2013

  53. [53]

    da Costa Teixeira, L

    J. da Costa Teixeira, L. Bourgeois, C.W. Sinclair, C.R. Hutchinson, The effect of shear - resistant, plate - shaped precipitates on the work hardening of Al alloys: Towards a predic tion of the strength – elongation correlation, Acta Materialia 57(20) (2009) 6075 - 6089

    work page 2009

  54. [54]

    Y . Gao, C. Yang, J. Zhang, L. Cao, G. Liu, J. Sun, E. Ma, Stabilizing nanoprecipitates in Al - Cu alloys for creep resistance at 300° C, Ma terials Reasearch Letters 7(

    work page